Polymer Network with Triple Shape Effect and Associated Programming Method

ABSTRACT

The invention relates to a polymer network with triple-shape-memory effect and an associated programming method. The invention also relates to a method for producing layer systems made of shape-memory materials comprising the polymer network. The polymer network includes
         A) a first crystalline switching segment made of a star polymer; and   B) a second crystalline switching segment made of a linear polymer or a star polymer.

The invention relates to a polymer network with triple-shape-memory effect and an associated programming method. The invention also relates to a method for producing layer systems made from polymer shape-memory materials.

STATE-OF-THE-ART AND BACKGROUND OF THE INVENTION

Unlike dual-shape-memory polymers which have been summarized in the literature and which can accomplish the network formation by both physical interactions as well as by covalent bonds, triple-shape-memory polymers have thus far been described only as networks based on covalent bonds [Bellin, I. et al., Polymer triple-shape materials, PNAS (2006), 103(48), p. 18043-18047]. Such triple-shape-memory polymer networks consist of at least one type of covalent cross-linking sites and at least two types of switching segments. In analogy to a dual-shape-memory polymer networks, triple-shape-memory polymer networks may contain, among others, segments of poly(ε-caprolactone), polyethers, polyether urethanes, polyimides, polyether imides, poly(meth)acrylate, polyurethane, polyvinyl compounds, polystyrenes, polyoxymethylene or poly(para-dioxanone). Introduction of hydrolysable groups, such as diglycolide, dilactide, polyanhydrides or polyorthoesters can produce biodegradable triple-shape-memory polymers [Lendlein, A. & Langer, R.: Biodegradable, elastic shape-memory polymers for potential biomedical applications. Science, 2002. 296(5573): p. 1673-1676, Lendlein, A. & Kelch, S.: Degradable, Multifunctional Polymer Biomaterials with Shape-memory. Materials Science Forum, 2005. 492-493: p. 219-224].

Polymer networks, which enable the triple-shape-memory effect, can be configured as AB-networks, where both chain segments contribute to the elasticity or as side chain networks, where the segments between the cross-linking sites predominantly contribute to the elasticity. The first may be realized, for example, by the polymerization of poly(ε-caprolactone)dimethacrylate with cyclohexylmethacrylate (MACL). A side chain network can be realized by the polymerization of poly(ε-caprolactone)dimethacrylate with polyethylene glycol monomethylether methacrylate (CLEG). Both network architectures are graphically illustrated in FIG. 1; (1) indicates here PCI-IMA segments; (2) PCL segments; (3) PEG side chains; and (4) cross-linking sites.

For programming purposes, segment of the test samples must be brought into a temporary form. The following exemplary methods may be used for programming:

-   -   Temporarily increasing the temperature above the switching         temperature(s) T_(switch) with subsequent deformation     -   Temporarily introducing plasticizers, so that the ambient         temperature is above T_(switch), with a subsequent deformation         and removal of the plasticizer.

Programming of a different segments of the component must here be performed separately for each segment of the component, whereby care has to be taken that the programming of a particular segment does not cancel the programming of another segment. The programming is done in dependence of the switching temperature. This means that in practice the segment with the highest T_(switch) is programmed first, whereafter the temperature is sequentially lowered, followed by programming of additional segments. In addition, different programming methods can be used for individual segments.

For retrieving the two shape changes of the component, the component must be moved into the heat-transmitting medium, wherein the temperature of the medium is successively increased, until the first shape change occurs. The additional shape change of the component occurs only when the temperature of the medium is increased further.

The principle of the triple-shape-memory polymers (or triple-shape polymers) has already been described in detail. Known segments are here based, on one hand, on the combination of segments made of polyethylene glycol (PEG) and poly(ε-caprolactone) (PCL) and, on the other hand, on the combination of PCL and cyclohexyl methacrylate (CHMA). The switching temperatures for using the triple-shape-memory effect are in the first case at 40 and 70° C. and in the second case at 70 and 130° C. In both cases, the shape change of components made from different material classes can only be stimulated through heat conduction of the air and hence takes a long time (40 to 80 minutes). Water is a very good heat transfer medium, but is not available for either polymer system, because it causes in PEG/PCL system swelling of the network due to the hydrophilic characteristic of PEG. Crystalline PEG regions may also swell, thereby negating the physical cross-linking required for the triple-shape-memory effect. In the PCL/CHMA system, water cannot be heated to the required switching temperature of 130° C. under normal pressure. Several applications, for example in the medical field, require complex shape changes, in particular those which includes a sequential order of the shapes A→B→C, sometimes within very short time intervals. It may for example be necessary to reshape a “round” tube into an “oval” tube and then back into a “round” tube. Until now, none of the aforedescribed triple-shape-memory polymers can produce this deformation in an aqueous environment. The shape changes attainable so far are limited by the programmable shapes, a movement of the test sample is so far only feasible to the extent to which this shape change has previously been programmed. In particular, two-dimensional or three-dimensional movements are severely limited. An additional disadvantage of the conventional systems is their low elasticity, in particular below the switching temperature.

The conventional systems have therefore the following disadvantages:

-   -   Until now, the use of the one-way shape-memory effect allows         only a one-time change of a shape by thermal stimulation. The         change of the stimulation conditions, for example an additional         increase of the temperature, has no effect on to the shape of a         component, if T_(perm) is not exceeded, which would cause         melting of the component with thermoplastics.     -   With the introduction of the triple-shape-memory polymers, it         becomes possible to realize all together three different shapes         of the component. The successive stimulation of the individual         shapes is attained by a temperature increase after suitable         programming of the component. However, programming of known         triple-shape-memory polymers is very demanding.     -   The material should provide high elasticity, i.e., high         elongation at break, in particular greater than 400% at room         temperature. However, known triple-shape-memory polymers have         significantly lower elasticity.     -   Known triple-shape-memory polymers are sensitive to water, so         that water is eliminated as a particularly effective heat         transfer medium. The swelling properties and switching         temperatures do not allow a shape change in water.

The aforementioned problems have so far not been solved, although the recently introduced concept of triple-shape-memory polymers has opened the possibility for sequential control of the thermally induced shape-memory effect. Neither a one-step programming of the triple-shape-memory effect at room temperature, nor a high elongation at break >400%, nor a variation of the trigger temperature through selection of the programming temperature have been realized to date with triple-shape-memory materials. It has also not been possible to date to make the triple-shape-memory effect reversible, renewed programming has so far been required after each shape recovery.

It is therefore an object of the invention to solve or at least alleviate one or more of the aforementioned problems.

SUMMARY OF THE INVENTION

A first aspect of the invention is to provide a polymer network with triple-shape-memory effect. The polymer network includes

A) a first crystalline switching segment made of a star polymer; and

B) a second crystalline switching segment made of a linear polymer or a star polymer.

In the present context, star polymers are defined as polymers with at least three linear side arms, connected to a central core. In other words, the term star polymer relates to polymers with a primary chain and at least one long chain branch or polymers with several long chain branches which are attached at a common branch point on the primary chain. Preferably, these are polymers with a total of three or four side arms.

The two crystalline switching segments are covalently bonded with each other in the polymer network. The triple-shape-memory materials according to the invention are therefore composed of at least two different macro-monomers. At least one macro-monomer must hereby be a star-shaped telechelic molecule, which has at least three side arms, each having a reactive end group. The second macro-monomer must be linear with at least two reactive end groups, or the two macro-monomers are star-shaped telechelic molecules. In addition, both phases must be crystalline. The triple-shape-memory material can be a multi-phase system, in which at least two phases are crystalline.

Preferably, the first crystalline switching segment is comprised of a star polymer based on poly(pentadecalactone) (PPDL segment). Independently, but more particularly in combination, the second crystalline switching segment may be comprised of a star polymer based on poly(ε-caprolactone) (PCL segment) or polytetrahydrofurane (PTHF segment).

In addition, in particular in combination with the aforementioned particular embodiments, polymer networks are preferred where the melting points of the two crystalline switching segments are in a range of 0° C. to 100° C., in particular in a range from room temperature to 100° C. Preferably, the melting points of the two crystalline switching segments are separated by at least 15° C., in particular by at least 20° C.

According to another preferred embodiment, the first crystalline switching segment and/or the second crystalline switching segment of the polymer network has an average molecular weight in a range from 500 to 50,000 g/mole, in particular in a range from 1000 to 5000 g/mole. These segments have a molecular weight in the aforementioned range particularly in polymer networks with PPDL, PCL or PTHF segments.

Preferably, the fraction of individual switching segments, in particular of the PPDL segments, as part of the total weight of all crystalline switching segments is 20 to 80 wt.-%. In particular, the fraction of the PPDL segments as part of the total weight of a polymer network with PPDL segments and PCL segments is 20 to 80 wt.-%.

The triple-shape material may be produced, for example, by synthesizing as a first intermediate product a star polymer based on poly(pentadecalactone) with functional end (terminal) groups arranged on the side arms (this preliminary stage can also be referred to as a nonlinear telechelic molecule with three or more arms). An important first intermediate product in the synthesis of the triple-shape-memory material is therefore in particular a star polymer based on poly(pentadecalactone) with a respective terminal functional group on each side arm. This star polymer based on poly(pentadecalactone) has preferably an average molecular weight in a range from 500 to 50,000 g/mole, in particular in a range from 1000 to 5000 g/mole. Basically, three methods are available for synthesizing the star polymers: (i) connecting prefabricated arms with a core, (ii) polymerization from a multi-functional initiator, and (iii) a combination of these two methods.

As a second intermediate product a linear polymer or a star polymer, for example based on poly(ε-caprolactone) or polytetrahydrofurane with likewise functional end groups arranged on the side arms, is used. This second polymer intermediate product has preferably an average molecular weight in a range from 500 to 50,000 g/mole, in particular in a range from 1000 to 25,000 g/mole.

The two polymer intermediate products are covalently linked via their terminal functional groups. The linkage can be either direct or via suitable coupling reagents (for example diisocyanates). More particularly, the linkage can also occur by a polyaddition reaction or through photopolymerization. Preferably, the functional group is a hydroxyl, acrylate or methacrylate group.

The invention offers, inter alia, the following advantages:

-   a. PPDL-based networks have a triple-shape-memory functionality,     which can be programmed at room temperature through cold stretching. -   b. By using water as heat transfer medium, triple-shape-memory     polymers can attain the temperatures required for shape changes     significantly more quickly than by using air as heat transfer     medium. -   c. By selecting a second switching segment which has a transition     temperature below the boiling temperature of water and is insoluble     in water, heat can now be transferred using water. -   d. The permanent shape in the polymer networks according to the     invention is formed already during the polymerization. The network     formation can here occur in particular through polymerization of     methacryl groups as well as through polycondensation of hydroxyl     groups with diisocyanates. The polymerization can be either     thermally initiated or photochemical. In particular, the     photochemical polymerization enables bodies with complex shapes,     because it is not performed from solution. -   e. PPDL-based networks, unlike the aforedescribed     triple-shape-memory networks, have significantly greater elasticity     and are also not soluble/swellable in water. -   f. Elongation fixation ratios and elongation recovery ratios have     values above 90%. -   g. Layers of the polymer networks can be differently programmed in     one dimension and are capable of realizing many three-dimensional     movements after being glued together covalently as a multilayer     system. -   h. The networks show under constant tension a thermally induced     reversible triple-shape-memory effect. High elongations of 100% and     more can be attained. This triple-shape-memory effect can be     reproduced without reprogramming as long as the sample is under     tension.

By using star-shaped PPDL oligomers, a network architecture is formed which due to the selection of the switching temperature has superior mechanical properties, such as elasticity, cold stretching ability and the selection of the trigger temperature, compared to the conventional systems. PPDL has always been used in conventional shape-memory networks as a hard segment. This is the first use of PPDL segments as switching segment. It is also the first triple-shape-memory network architecture in which two crystalline primary chain segments are used which contribute to the overall elasticity of the network. The structure of multilayer systems enables a significant broadening of possible shape changes, thus significantly enlarging the spectrum of applications for the polymers.

Components produced from a uniform triple-shape-memory polymer can be intentionally switched with a time offset by increasing the ambient temperature in an aqueous environment. With the one-step programming of triple-shape-memory networks with a crystalline and a glassy segment, recovery of the programming after a certain time has been observed. Triple-shape-memory networks with two crystalline segments, wherein both crystalline phases contribute to the total elasticity, do not exhibit this undesirable recovery.

By using triple-shape-memory polymers with several switching segments, two consecutive shape transitions can be realized in a polymer.

Additional Aspects of the Invention are:

-   A) New approaches for network synthesis     -   1. The networks are built from two different star-shaped         telechelic molecules, or     -   2. The networks are built from a star-shaped telechelic molecule         and a linear telechelic molecule. -   B) PPDL segments are used for the networks     -   1. PPDL is insoluble in water     -   2. PPDL has a melting temperature below 100° C. -   C) PPDL-based shape-memory systems have high elasticity     -   1. PPDL-based shape-memory systems allow programming by cold         stretching     -   2. PPDL-based shape-memory systems allow a noticeable increase         in elongation when crystallizing under tension -   D) PCL and PPDL segments are covalently cross-linked     -   1. The network architecture allows the creation of a temperature         shape-memory effect over a wide temperature range (room         temperature to T_(m,PPDL)).

The polymer network based on star-shaped segments of poly(pentadecadolactone) (PPDL) can perform several shape change steps. These are characterized by the following aspects

(1) High elasticity at room temperature (RT) (2) The triple-shape-memory effect can be programmed at ambient temperature (T<T_(m,PPDL)) by cold stretching (3) Programming can be performed as one-step programming.

Combinations are possible which allow a temperature shape-memory effect for one of the two switching faces. A multilayer architecture of sample bodies allows complex three-dimensional shape changes. Combinations are also possible which show a reversible triple-shape-memory effect after pre-stretching under constant tension.

According to another aspect of the invention, a method is provided for programming a polymer network with triple-shape-memory effect of the aforedescribed composition. The programming method includes the step of:

Programming of at least two different shapes of the polymer network with

-   -   a) A two-step method;     -   b) A one-step method;     -   c) Cold stretching;     -   d) A combination of heating and cold stretching; or     -   e) Preconditioning by stretching.

In particular, programming can be performed according to the two-step method, wherein the polymer network is heated to T_(high) above the two melting temperatures T_(m,1) and T_(m,2) of the crystalline switching segments (T_(m,1)<T_(m,2)), deformed, cooled to a temperature below T_(m,2), deformed again, and then cooled to a temperature T_(m,1).

Programming can also be performed according to the one-step method, wherein the polymer network is heated to T_(high) above the two melting temperatures T_(m,1) and T_(m,2) of the crystalline switching segments <T_(m,2)), deformed and then cooled to a temperature below T_(m,1). The recovery occurs during heating to T_(high). First, a recovery occurs at T_(sw,1), and then upon further heating at T_(sw,2).

Programming can also be performed by cold stretching, wherein the polymer network is deformed at a temperature T_(low) below the two melting temperatures T_(m,1) and T_(m,2) of the crystalline switching segments (T_(low)<<T_(m,1)<T_(m,2)). The recovery occurs during heating to T_(high). First, a recovery occurs at T_(sw,1) and then upon further heating at T_(sw,2).

Programming can also be performed by a combination of heating and cold stretching, wherein the polymer network is deformed at a temperature T_(mid) which is between the two melting temperatures T_(m,1) and T_(m,2) of the crystalline switching segments (T_(m,1)<T_(mid)<T_(m,2)). The recovery occurs during heating to T_(high). First, a recovery occurs at T_(sw,1), and thereafter upon further heating at T_(sw,2).

Programming can also be performed with preconditioning by stretching at T_(high). If the tension is kept constant even after stretching, then two shapes are stepwise attained by expansion when cooling to T_(low), which are characterized by the two crystallization temperatures T_(c,1) and T_(c,2) (T_(high)>T_(c,1)>T_(c,2)>T_(low)), allowing reversible switching between three shapes. The extent of stretching hereby determines the deformation during cooling. The recovery occurs during heating to T_(high) under constant tension. Initially, there is a recovery at T_(sw,1) and upon further heating at T_(sw,2). Switching between the shapes by cooling and heating can be arbitrarily repeated under constant tension, without requiring an additional programming step.

The recovery can take place under tension or by heating without tension across both T_(sw). In particular, this can take place in water. Another aspect of the invention therefore relates to a method for recovering a programmed polymer network with triple-shape-memory effect, which includes step of thermal treatment of the programmed polymer network in water as thermal medium.

By selecting the programming temperature, the switching temperature of a shape-memory transition in the melting region of the two crystalline phases can be arbitrarily set.

Preferably, several layers of the polymer networks are joined with one another. The layers can be programmed identically or may have different magnitude, direction or programming temperature. Accordingly, tension gradients of different magnitude and direction can thus be generated in the multilayer material at different T_(switch), which can result in complex shape changes.

If thin layers of the triple-shape-memory polymer, which have been subjected to different programming with respect to magnitude or direction, are covalently glued together, then this multilayer test sample can perform highly complex movements when the shape-memory effect is activated.

For realizing complex three-dimensional shape changes, only one-dimensional programming steps are required for the polymer layers which are then joined according to a calculated architecture. In this way, shapes can be attained which are difficult or impossible when programmed on bulk test samples. The attainable shapes are further augmented by using triple-shape-memory materials.

If tension is maintained in one or several layers that have been glued together from previously programmed layers, then the complex three-dimensional shape changes are completely or partially reversible.

Another aspect of the invention therefore relates to a method for producing layer systems from polymer shape-memory materials with the steps:

-   a) Providing at least two layers made of polymer shape-memory     materials; and -   b) Producing a layer system from the at least two layers by reactive     gluing, wherein the two layers differ with respect to their     programming, shape or composition.

The layers can be provided in planar form or with a three-dimensional profile. The layers can have a different layer thickness. The layers may also consist of a polymer matrix with integrated shape-memory polymer fibers. The layers can also have different degrees of programming, in particular degrees of stretching, and/or a different programming orientation. Lastly, the layers can be programmed mono-directionally or multi-directionally.

Other preferred embodiments of the invention are recited as additional features in the dependent claims.

Exemplary embodiments of the invention will now be described with reference to the appended drawings. These show in:

FIG. 1 conventional polymer network architectures, namely (a) a MACL network and (b) a CLEG network;

FIG. 2A a network architecture of a system according to the invention and its representation according to a first embodiment;

FIG. 2B a network architecture of a system according to the invention and its representation according to a second embodiment;

FIGS. 3 to 5 layer systems made of polymer shape-memory materials in different variants; and

FIG. 6 reversible triple-shape-memory properties of the network a: T-PPDL(4)-PCL(8,50) at a tension of 0.6 MPa; b: T-PPDL(3)-PCL(8,50) at a tension of 1 MPa.

The synthesis of the hydroxy-telechelic star polymers with PCL- or PPDL-side arms occurs through ring opening polymerization of ε-caprolactone or pentadecadolactone with tri- or tetra-functional initiators. The synthesis can occur according to the following description: Arvanitoyannis, I., et al.: Novel Star-Shaped Polylactide with Glycerol Using Stannous Octoate or Tetraphenyl Tin as Catalyst 1. Synthesis, Characterization and Study of Their Biodegradability, Polymer, 1995, 36(15), p. 2947-2956. However, in contrast to this reference, the ring opening polymerization of PPDL was performed in 14 to 21 days. Hydroxy-telechelic star polymers with PTHF side arms can also be synthesized in an analogous manner.

Examples for structures of polymer networks made of star-shaped telechelic molecules are illustrated in FIGS. 2A and 2B.

Synthesis of hydroxy-telechelic oligo(ε-caprolactone) PCL(x)-OH

97 ml ε-caprolactone, 0.68 g pentaerythrite and 280 mg dibutyltinoxide (DBTO) were reacted while stirring in a Schlenk flask in hydrogen atmosphere at 130° C. After a polymerization time of 7 h the reaction mixture is cooled to room temperature. The oligomers are dissolved in an approximately sixfold volume excess of dichloromethane. The reaction product is precipitated by slowly dripping the solution into an approximately tenfold volume excess of hexane fraction under strong stirring. The precipitate is washed with hexane fraction and dried at 25° C. in vacuum (approximately 1 mbar) until attaining constant weight. The molar mass and functional groups as well as the thermal properties were analyzed by determining the OH-number, GPC, ¹H-NMR and DSC. The OH-number determination yielded M_(n)=22,700 g mole⁻¹. DSC measurements gave a melting temperature of 54.5° C., ΔH 76.8 J*g⁻¹. The obtained oligo(ε-caprolactone) with M_(n) of about 20,000 g/mol will subsequently be referred to as PCL(20)-OH.

The synthesis of the hydroxy-telechelic oligo(ε-caprolactone)s PCL(4)-OH with M_(n) 4000 g·mole⁻¹ or the hydroxy-telechelic oligo(ε-caprolactone)s PCL(8)-OH with M_(n) 8000 g·mole⁻¹ took place via ring opening polymerization of ε-caprolactone similar to PCL(20)-OH. PCL(8)-OH is also commercially available under the label CAPA4801.

Synthesis of hydroxyl-telechelic oligo(pentadecadolactone) PPDL(y)-OH

112.5 g pentadecadolactone, 3.375 g 1,1,1-tris(hydroxymethyl)ethane (optionally also other tri- or tetra-functional initiators) and DBTO 105 mg were reacted while stirring in a Schlenk flask in a nitrogen atmosphere at 130° C. After a polymerization time of 7 h the reaction mixture is cooled to room temperature. The oligomers are dissolved in an approximately sixfold volume excess of dichloromethane. The reaction product is precipitated by slowly dripping the solution into an approximately tenfold volume excess of hexane fraction under strong stirring. The precipitate is washed with hexane fraction and dried at 50° C. in vacuum (approximately 1 mbar) until attaining constant weight.

The molar mass and functional groups as well as the thermal properties were analyzed by determining the OH-number, GPC, ¹H-NMR and DSC. The OH-number determination yielded M_(n)=4000 g mole⁻¹. DSC measurements detected two melting temperatures of 49.8° C. and 84.8° C., ΔH 109.5 J·g⁻¹. The obtained oligo(pentadecadolactone) with M_(n) of about 4000 g/mol will subsequently be referred to as PPDL(4)-OH.

The synthesis of the hydroxy-telechelic oligo(pentadecadolactone)s PPDL(3)-OH with M_(n) 3000 g·mole⁻¹ or of the hydroxy-telechelic oligo(pentadecadolactone)s PPDL(2)-OH with M_(n) 2000 g·mole⁻¹ was performed similar to the synthesis of PPDL(4)-OH.

Synthesis of oligo(ε-caprolactone)tetramethacrylate PCL(x)-IEMA

50.0 g PCL(20)-OH, 1.6 ml IEMA and 6.5 μL dibutyltin(IV)dilaurate were dissolved in 250 ml dichloromethane under argon and stirred at room temperature for 5 days. The reaction product is precipitated by slowly dripping the solution into an approximately tenfold volume excess of hexane fraction under strong stirring. The precipitate is washed with hexane fraction and dried at 25° C. in vacuum (approximately 1 mbar) until attaining constant weight. ¹H-NMR showed that the OH-groups in PCL(20)-OH have completely reacted with IEMA. The obtained oligo(ε-caprolactone)tetramethacrylate will subsequently be referred to as PCL(20)-IEMA.

The synthesis of the oligo(ε-caprolactone)tetramethacrylate PCL(4)-IEMA with M_(n) 4000 g·mole⁻¹ and of the oligo(ε-caprolactone)tetramethacrylates PCL(8)-IEMA with M_(n) 8000 g·mole⁻¹ was performed similar to PCL(20)-IEMA.

Synthesis oligo(pentadecadolactone)trimethacrylate PPDL(y)-IEMA

50.0 g PPDL(4)-OH, 6.1 ml IEMA and 25.4 μL dibutyltin(IV)dilaurate were dissolved in 250 ml dichloromethane under argon and stirred at room temperature for 5 days. The reaction product is precipitated by slowly dripping the solution into an approximately tenfold volume excess of hexane fraction under strong stirring. The precipitate is washed with hexane fraction and dried at 25° C. in vacuum (approximately 1 mbar) until attaining constant weight. It was demonstrated with ¹H-NMR that the OH-groups in PPDL(4)-OH have completely reacted with IEMA. The obtained oligo(pentadecadolactone)trimethacrylate will subsequently be referred to as PPDL(4)-IEMA.

Synthesis of the Networks According to the Polycondensation Method A)

The produced star polymers PCL(x)-OH and PPDL(y)-OH were dissolved in dichloromethane with a suitable mixing ratio. 2,2,4- and 2,4,4-trimethylhexane-1,6-diisocyanate (TMDI) is added as cross-linker. Mixtures with 25-75 wt.-% PPDL(y)-OH have proven to be suitable mixing ratios for triple-shape-memory polymers.

The hydroxy-telechelic oligomers are dissolved with an approximately tenfold excess mass of dichloromethane under nitrogen. Diisocyanate is added to the solution while stirring. The quantity of diisocyanate corresponds here to a molar ratio of the isocyanate to hydroxyl groups of 1.05 to 1.00. The calculation in Table 1 is based on the average value of the molar mass of the hydroxyl functionality of the polymer educts determined by ¹H-NMR spectroscopy, for example of PPDL(4)-OH or PCL(20)-OH. The reaction mixture was stirred for five minutes at room temperature and filled into PTFE trays. Approximately 20 ml of the solution are introduced when using trays with an inside diameter of about 100 mm. A continuous nitrogen flow is passed over the solutions for 24 h at 60° C. so as to carefully evaporate the solvent during the film formation. Thereafter, the films are heated under vacuum (about 100 mbar) for 4 days to 80° C. The raw products of the poly-addition reactions are, unless otherwise stated, swollen in chloroform, thus determining the gel content and the degree of swelling, and dried at 80° C. in vacuum (1 mbar) until attaining constant weight. The weights of the oligomers and the diisocyanate and the gel content of the networks are listed in Table 1.

TABLE 1 Approaches for producing the networks from PCL(4)-OH, PCL(8)-OH, PCL(20)-OH, PPDL(2)-OH, PPDL(3)-OH, PPDL(4)-OH and TMDI according to the polycondensation method A) (indicated by the prefix T); network designation: PPDL(x)-PCL(y, z) are polymer networks made from the following star-shaped pre-polymers: 3-arm PPDL with Mn about x · 1000 g/mole and 4-arm PCL with M_(n) about y · 1000 g/mole and a fraction of z mass-%; Degree of PPDL(y)- PCL(20)- PCL(8)- PCL(4)- swelling OH OH OH OH TMDI μ_(PPDL) Content in chloroform Designation (g) (g) (g) (g) (ml) (wt.-%) (wt.-%) (wt.-%) T-PPDL(4) 1.50 — — — 0.070 100 91 1420 T-PPDL(4)- 0.75 2.25 — — 0.106 25 85 2220 PCL(20, 75) T-PPDL(4)- 1.2 1.8 — — 0.113 40 85 1980 PCL(20, 60) T-PPDL(4)- 1.5 1.5 — — 0.118 50 88 1750 PCL(20, 50) T-PPDL(4)- 1.8 1.2 — — 0.122 60 85 1960 PCL(20, 40) T-PPDL(4)- 2.25 0.75 — — 0.141 75 92 1440 PCL(20, 25) T-PPDL(4)- 0.75 — 2.25 — 0.148 25 98 830 PCL(8, 75) T-PPDL(4)- 1.2 — 1.8 — 0.146 40 97 970 PCL(8, 60) T-PPDL(4)- 1.5 — 1.5 — 0.145 50 95 1240 PCL(8, 50) T-PPDL(4)- 1.8 — 1.2 — 0.144 60 92 1820 PCL(8, 40) T-PPDL(4)- 2.25 — 0.75 — 0.143 75 92 1310 PCL(8, 25) T-PPDL(4)- 0.75 — — 2.25 0.26 25 97 1100 PCL(4, 75) T-PPDL(4)- 1.2 — — 1.8 0.236 40 93 1350 PCL(4, 60) T-PPDL(4)- 1.5 — — 1.5 0.22 50 94 1360 PCL(4, 50) T-PPDL(4)- 1.8 — — 1.2 0.204 60 92 1280 PCL(4, 40) T-PPDL(4)- 2.25 — — 0.75 0.18 75 94 1220 PCL(4, 25) T-PPDL(3)- 0.75 2.25 — — 0.106 25 85 2080 PCL(20, 75) T-PPDL(3)- 1.5 1.5 — — 0.186 50 84 1940 PCL(20, 50) T-PPDL(3)- 2.25 0.75 — — 0.250 75 90 1250 PCL(20, 25) T-PPDL(3)- 0.75 — 2.25 — 0.200 25 98 800 PCL(8, 75) T-PPDL(3)- 1.5 — 1.5 — 0.238 50 97 790 PCL(8, 50) T-PPDL(3)- 2.25 — 0.75 — 0.275 75 98 800 PCL(8, 25) T-PPDL(3)- 0.75 — — 2.25 0.302 25 95 1050 PCL(4, 75) T-PPDL(3)- 1.5 — — 1.5 0.306 50 96 880 PCL(4, 50) T-PPDL(3)- 2.25 — — 0.75 0.309 75 97 830 PCL(4, 25) T-PPDL(2)- 0.75 2.25 — — 0.138 25 90 1620 PCL(20, 75) T-PPDL(2)- 1.5 1.5 — — 0.215 50 88 1710 PCL(20, 50) T-PPDL(2)- 2.25 0.75 — — 0.293 75 95 1170 PCL(20, 25) T-PPDL(2)- 0.75 — 2.25 — 0.214 25 98 800 PCL(8, 75) T-PPDL(2)- 1.5 — 1.5 — 0.66 50 98 820 PCL(8, 50) T-PPDL(2)- 2.25 — 0.75 — 0.318 75 97 920 PCL(8, 25) T-PPDL(2)- 0.75 — — 2.25 0.317 25 96 1040 PCL(4, 75) T-PPDL(2)- 1.5 — — 1.5 0.334 50 96 1030 PCL(4, 50) T-PPDL(2)- 2.25 — — 0.75 0.352 75 93 1100 PCL(4, 25)

Synthesis of the Networks with the Polymerization Method B)

The produced hydroxy-telechelic star polymers PCL(x)-IEMA or PPDL(y)-IEMA are melted and mixed, whereafter a thermal radical initiator (AIBN, BPO) is added. Here too, mixtures with 25-75 wt.-% PPDL have been found to be suitable for triple-shape-memory polymer mixtures. Polymerization can alternatively also occur photochemically. The functionalized oligomers are hereby melted, a 1 mole-% photo initiator is added, the mixture is then mixed and photo-polymerized by irradiation with a Hg-lamp.

TABLE 2 Approaches for preparing the networks from PCL(20)-IEMA and PPDL(4)-IEMA according to the polymerization method B) (indicated by the prefix P). Degree of PPDL(4)- PCL(8)- PCL(20)- swelling IEMA IEMA IEMA μ_(PPDL) Gel content in chloroform Designation (g) (g) (g) (wt.-%) (wt.-%) (wt.-%) P-PPDL(4)-PCL(20, 75) 0.75 — 2.25 25 87 840 P-PPDL(4)-PCL(20, 60) 1.20 — 1.80 40 58 1660 P-PPDL(4)-PCL(20, 50) 1.50 — 1.50 50 71 1050 P-PPDL(4)-PCL(20, 40) 1.80 — 1.20 60 54 1420 P-PPDL(4)-PCL(20, 25) 2.25 — 0.75 75 78 1000 P-PPDL(4)-PCL(20, 12) 2.625 — 0.375 88 87 650 P-PPDL(4)-PCL(8, 75) 0.75 2.25 — 25 88 620 P-PPDL(4)-PCL(8, 60) 1.20 1.8 — 40 70 900 P-PPDL(4)-PCL(8, 50) 1.50 1.5 — 50 87 590 P-PPDL(4)-PCL(8, 40) 1.80 1.2 — 60 65 980 P-PPDL(4)-PCL(8, 25) 2.25 0.75 — 75 77 850

Thermal Properties of the Polymer Networks

The networks from PPDL and PCL with M_(n) of 4000 g·mole⁻¹, 8000 g·mole⁻¹ and 20,000 g·mole⁻¹ have in DSC experiments to melting ranges in a temperature region from −100° C. to 100° C. They can therefore be considered as semi-crystalline systems. Tables 3 shows the thermal properties of the polymer networks. The two melting temperatures can be used as two T_(trans) for the triple-shape effect.

TABLES 3 Thermal properties of the polymer networks according to the polycondensation method A) μ_(PPDL) T_(g) T_(m1) T_(m2) ΔH₁ ^(b)) ΔH_(PCL) ^(c)) ΔH₂ ^(b)) ΔH_(PPDL) ^(c)) Designation [wt.-%] [° C.] [° C.] [° C.] [J · g⁻¹] [J · g⁻¹] [J · g⁻¹] [J · g⁻¹] T-PPDL(4) 100 n.d. — 79.4 — — 99.4 99.4 T-PPDL(4)-PCL(20, 75) 25 n.d. 55.1 74.8 56.0 74.7 20.5 82.0 T-PPDL(4)-PCL(20, 60) 40 n.d. 54.3 76.9 40.6 67.7 30.7 76.8 T-PPDL(4)-PCL(20, 50) 50 n.d. 52.6 77.1 29.4 58.8 40.2 80.4 T-PPDL(4)-PCL(20, 40) 60 n.d. 53.5 79.1 32.8 82.0 53.3 88.8 T-PPDL(4)-PCL(20, 25) 75 n.d. 52.0 78.6 18.8 75.2 64.0 85.3 T-PPDL(4)-PCL(8, 75) 25 −54.6 36.9 72.5 39.0 52.0 21.3 85.2 T-PPDL(4)-PCL(8, 60) 40 −55.2 38.6 74.2 33.9 56.5 29.9 74.8 T-PPDL(4)-PCL(8, 50) 50 n.d. 39.9 77.5 30.4 60.8 44.0 88.0 T-PPDL(4)-PCL(8, 40) 60 n.d. 42.3 79.1 25.4 63.5 51.9 86.5 T-PPDL(4)-PCL(8, 25) 75 n.d. 42.8 79.5 17.6 70.4 71.1 94.8 T-PPDL(4)-PCL(4, 75) 25 −47.8 31.0 71.7 34.0 45.3 19.2 76.8 T-PPDL(4)-PCL(4, 60) 40 n.d. 34.5 77.1 33.7 56.2 34.7 86.8 T-PPDL(4)-PCL(4, 50) 50 n.d. 33.1 75.1 24.0 48.0 46.2 92.4 T-PPDL(4)-PCL(4, 40) 60 n.d. 31.9 75.3 18.3 45.3 55.8 93.0 T-PPDL(4)-PCL(4, 25) 75 n.d. n.d. 78.7 n.d. n.d. 66.4 88.5 T-PPDL(3)-PCL(20, 75) 25 −57.5 56.4 71.6 53.9 71.9 15.1 60.4 T-PPDL(3)-PCL(20, 50) 50 n.d. 54.0 73.4 40.6 81.2 36.8 73.6 T-PPDL(3)-PCL(20, 25) 75 n.d. 53.9 74.6 30.2 120.8 53.4 71.2 T-PPDL(3)-PCL(8, 75) 25 −53.0 36.2 65.5 38.8 51.1 14.0 56.0 T-PPDL(3)-PCL(8, 50) 50 n.d. 32.7 61.6 28.6 57.2 39.4 78.8 T-PPDL(3)-PCL(8, 25) 75 n.d. 32.8 73.4 14.6 58.4 59.9 79.9 T-PPDL(3)-PCL(4, 75) 25 −46.4 29.8 67.3 36.8 49.1 16.9 67.6 T-PPDL(3)-PCL(4, 50) 50 n.d. 27.1 72.0 24.6 49.2 40.5 81.0 T-PPDL(3)-PCL(4, 25) 75 n.d. n.d. 68.7 — — 70.6 70.6 T-PPDL(2)-PCL(20, 75) 25 n.d. 55.0 n.d. 66.1 66.1 — — T-PPDL(2)-PCL(20, 50) 50 n.d. 54.2 64.5 49.8 99.6 22.8 45.6 T-PPDL(2)-PCL(20, 25) 75 n.d. n.d. 61.6 — — 67.4 67.4 T-PPDL(2)-PCL(8, 75) 25 −51.4 35.0 53.7 45.2 60.3  6.3 25.2 T-PPDL(2)-PCL(8, 50) 50 n.d. 31.3 54.0 30.4 60.8 23.6 47.2 T-PPDL(2)-PCL(8, 25) 75 n.d. n.d. 58.4 — — 63.0 63.0 T-PPDL(2)-PCL(4, 75) 25 −45.2 27.7 52.8 40.6 54.1 11.1 44.4 T-PPDL(2)-PCL(4, 50) 50 n.d. 28.3 57.7 18.7 37.4 27.7 55.4 T-PPDL(2)-PCL(4, 25) 75 n.d. n.d. 63.5 — — 65.7 65.7

TABLE 4 Thermal properties of the polymer networks according to the polymerization method B) μ_(PPDL) T_(m1) T_(m2) ΔH₁ ΔH₂ Designation wt.-% ° C. ° C. J/g J/g P-PPDL(4)-PCL(20, 75) 25 47.0 68.6 50.7 15.0 P-PPDL(4)-PCL(20, 60) 40 54.1 67.9/83.5 46.5 27.6 P-PPDL(4)-PCL(20, 50) 50 53.7 70.0/83.8 32.6 46.1 P-PPDL(4)-PCL(20, 40) 60 54.1 74.1/84.3 20.3 63.0 P-PPDL(4)-PCL(20, 25) 75 52.9 81.7 22.7 47.1 P-PPDL(4)-PCL(20, 12) 88 51.8 87.7 19.5 53.8 P-PPDL(4)-PCL(8, 75) 25 43.3 67.9 14.3 30.6 P-PPDL(4)-PCL(8, 60) 40 47.2 71.7/81.5 24.8 51.9 P-PPDL(4)-PCL(8, 50) 50 20.9 67.9 16.7 38.0 P-PPDL(4)-PCL(8, 40) 60 46.5 70.4 — 66.9 P-PPDL(4)-PCL(8, 25) 75 46.4 73.0/82.2 16.1 74.8

Mechanical Properties of the Polymer Networks

The mechanical properties of the networks are determined at 25° C., 60° C. and 100° C. by performing tensile tests. Whereas semi-crystalline materials are present at 25° C., the networks are in a rubber-elastic state at 100° C. Both temperature ranges are relevant for an application as shape-memory material, because they determine below T_(trans) the mechanical properties of the test sample in the permanent and temporary shape before programming and before completed recovery. However, the mechanical properties above T_(trans) are important with regard to programming of the temporary shape. With tensile tests at 60° C., the mechanical properties of the materials are also measured at the temperature which is to be selected for programming the second shape.

At 25° C., the mechanical properties are determined by the glassy state of the materials. The networks from PPDL, PCL and TMDI show in tensile tests a yield point accompanied by constriction of the sample.

The E-modules E have values between 134 MPa and 430 MPa. The tensile strength σ_(max) is in a range from 15 MPa to 31 MPa at elongations ε_(max) of 6% to 16%. The observed average values for the elongation at break ε_(b) are between 400% and 1000%. The mechanical characteristics of the investigated networks according to the poly-condensation method A) are listed in Table 5.

TABLE 5 Mechanical properties of the polymer networks according to poly-condensation method A at 25° C., 60° C. and 100° C. μ_(PPDL) 25° C. 60° C. 100° C. [wt E σ_(b) ε_(b) E σ_(b) ε_(b) E σ_(b) ε_(b) Designation %] [MPa] [MPa] [%] [MPa] [MPa] [%] [MPa] [MPa] [%] T-PPDL(4) 100 370 ± 87 20.9 ± 2.6 523 ± 35 102 ± 16  9.9 ± 1.2 690 ± 54 0.65 ± 0.13 1.25 ± 0.21 561 ± 68 T-PPDL(4)-PCL(20, 75) 25 273 ± 20 29.5 ± 2.3 717 ± 22 15.8 ± 1.3  4.8 ± 0.7 441 ± 26 1.84 ± 0.28 1.33 ± 0.12 171 ± 43 T-PPDL(4)-PCL(20, 60) 40 332 ± 24 24.6 ± 3.9 621 ± 86 22.4 ± 3.3  6.8 ± 1.4 484 ± 38 2.16 ± 0.30 1.80 ± 0.20 254 ± 45 T-PPDL(4)-PCL(20, 50) 50 319 ± 16 30.4 ± 3.5 715 ± 43 28.9 ± 2.6  6.3 ± 0.9 463 ± 24 1.88 ± 0.26 1.91 ± 0.16 199 ± 21 T-PPDL(4)-PCL(20, 40) 60 272 ± 20 28.5 ± 4.7 692 ± 59 23.3 ± 4.1  12.5 ± 2.6  588 ± 47 2.08 ± 0.60 1.18 ± 0.28 117 ± 7  T-PPDL(4)-PCL(20, 25) 75 300 ± 15 32.4 ± 4.2 664 ± 59 35.1 ± 3.0  8.2 ± 0.8 489 ± 22 2.36 ± 0.22 1.43 ± 0.22 151 ± 30 T-PPDL(4)-PCL(8, 75) 25 101 ± 16 20.3 ± 4.0 587 ± 49 8.0 ± 0.7 5.0 ± 0.8 292 ± 48 3.75 ± 0.35 2.12 ± 0.31 126 ± 20 T-PPDL(4)-PCL(8, 60) 40 185 ± 18 27.8 ± 4.3 665 ± 59 7.3 ± 1.3 6.1 ± 0.7 471 ± 30 3.25 ± 0.08 1.92 ± 0.23 159 ± 41 T-PPDL(4)-PCL(8, 50) 50 207 ± 18 23.6 ± 2.6 764 ± 29 12.7 ± 2.5  7.5 ± 0.9 616 ± 23 2.41 ± 0.31 1.23 ± 0.25 103 ± 18 T-PPDL(4)-PCL(8, 40) 60 257 ± 49 24.8 ± 3.5 707 ± 85 21.1 ± 6.7  6.3 ± 2.0 549 ± 43 1.97 ± 0.20 1.33 ± 0.13 206 ± 54 T-PPDL(4)-PCL(8, 25) 75 340 ± 33 25.8 ± 2.5 693 ± 46 45.8 ± 8.4  9.1 ± 1.1 557 ± 62 1.79 ± 0.12 1.22 ± 0.18 230 ± 52 T-PPDL(4)-PCL(4, 75) 25  73 ± 15 20.5 ± 2.0 673 ± 28 6.7 ± 0.9 2.9 ± 0.6 151 ± 40 3.38 ± 0.26 1.33 ± 0.10  65 ± 10 T-PPDL(4)-PCL(4, 60) 40 179 ± 17 27.1 ± 2.5 714 ± 27 16.1 ± 5.8  3.4 ± 0.5 228 ± 39 2.98 ± 0.11 1.54 ± 0.07 103 ± 9  T-PPDL(4)-PCL(4, 50) 50 131 ± 21 21.2 ± 3.4 486 ± 42 18.2 ± 3.8  4.3 ± 1.0 263 ± 37 2.53 ± 0.21 1.80 ± 0.14 206 ± 40 T-PPDL(4)-PCL(4, 40) 60 154 ± 10 24.9 ± 1.9 562 ± 32 34.1 ± 7.0  7.5 ± 1.9 346 ± 40 2.23 ± 0.12 1.33 ± 0.16 155 ± 30 T-PPDL(4)-PCL(4, 25) 75 274 ± 22  253 ± 3.9 691 ± 57 59.8 ± 6.2  8.9 ± 0.7 521 ± 39 1.47 ± 0.13 1.01 ± 0.16 188 ± 48 T-PPDL(3)-PCL(20, 75) 25 305 ± 43 25.2 ± 3.5 691 ± 51 2.3 ± 0.2 2.3 ± 0.3 457 ± 50 0.87 ± 0.07 0.95 ± 0.13 286 ± 62 T-PPDL(3)-PCL(20, 50) 50 282 ± 21 19.7 ± 2.7 543 ± 36 10.5 ± 0.9  3.8 ± 0.2 461 ± 19 0.92 ± 0.02 0.83 ± 0.06 235 ± 23 T-PPDL(3)-PCL(20, 25) 75 242 ± 23 31.2 ± 5.0 595 ± 53 20.7 ± 1.9  8.4 ± 1.3 503 ± 39 1.79 ± 0.10 1.20 ± 0.10 146 ± 22 T-PPDL(3)-PCL(8, 75) 25 37 ± 7 11.0 ± 2.9 425 ± 99 4.3 ± 0.3 2.3 ± 0.2 140 ± 24 4.82 ± 0.19 1.72 ± 0.35  57 ± 17 T-PPDL(3)-PCL(8, 50) 50  64 ± 12 15.9 ± 1.9 433 ± 26 9.9 ± 0.6 4.4 ± 0.5 226 ± 32 4.29 ± 0.19 1.62 ± 0.23  62 ± 17 T-PPDL(3)-PCL(8, 25) 75  97 ± 13 23.7 ± 2.3 437 ± 23 3.9 ± 0.1 5.9 ± 0.9 260 ± 46 3.70 ± 0.10 1.82 ± 0.19  92 ± 16 T-PPDL(3)-PCL(4, 75) 25 58 ± 9 20.8 ± 4.5 525 ± 48 3.0 ± 0.4 1.7 ± 0.2 140 ± 36 2.60 ± 0.11 1.07 ± 0.16  67 ± 15 T-PPDL(3)-PCL(4, 50) 50  67 ± 10 18.6 ± 3.5 423 ± 57 12.9 ± 1.5  4.6 ± 0.7 164 ± 43 3.40 ± 0.12 1.47 ± 0.11 69 ± 9 T-PPDL(3)-PCL(4, 25) 75  84 ± 11 23.4 ± 6.9 405 ± 47 19.7 ± 1.3  6.1 ± 0.4 195 ± 11 3.75 ± 0.11 1.67 ± 0.38  83 ± 30 T-PPDL(2)-PCL(20, 75) 25 178 ± 55 17.2 ± 5.5 684 ± 91 1.5 ± 0.2 2.0 ± 0.4 521 ± 68 1.44 ± 0.07 1.04 ± 0.20 188 ± 64 T-PPDL(2)-PCL(20, 50) 50 206 ± 12 24.4 ± 3.2 784 ± 52 4.3 ± 0.9 3.7 ± 0.5 614 ± 51 1.28 ± 0.07 0.97 ± 0.09 207 ± 36 T-PPDL(2)-PCL(20, 25) 75 134 ± 10 26.6 ± 4.4 649 ± 20 5.7 ± 1.9 4.7 ± 1.1 463 ± 34 2.28 ± 0.08 1.16 ± 0.15 110 ± 30 T-PPDL(2)-PCL(8, 75) 25 23 ± 4  9.7 ± 1.4 384 ± 49 4.0 ± 0.1 2.0 ± 0.4 107 ± 35 4.74 ± 0.29 1.36 ± 0.36  42 ± 20 T-PPDL(2)-PCL(8, 50) 50  52 ± 12 13.6 ± 2.5 459 ± 70 3.4 ± 0.2 2.0 ± 0.5 141 ± 58 4.03 ± 0.17 1.53 ± 0.34  66 ± 22 T-PPDL(2)-PCL(8, 25) 75  76 ± 10 24.0 ± 6.2 605 ± 34 3.1 ± 0.2 2.7 ± 0.6 270 ± 68 3.18 ± 0.21 1.33 ± 0.23  71 ± 18 T-PPDL(2)-PCL(4, 75) 25  18 ± 12 15.8 ± 3.6 502 ± 31 2.6 ± 0.2 1.5 ± 0.4 110 ± 42 2.68 ± 0.06 1.11 ± 0.13  67 ± 13 T-PPDL(2)-PCL(4, 50) 50 15 ± 3 19.1 ± 3.1 606 ± 23 3.1 ± 0.3 1.9 ± 0.2 161 ± 21 2.84 ± 0.05 1.07 ± 0.19  59 ± 18 T-PPDL(2)-PCL(4, 25) 75  65 ± 17 21.8 ± 3.1 616 ± 67 3.6 ± 0.5 3.8 ± 0.4 396 ± 44 1.99 ± 0.07 0.92 ± 0.11  76 ± 16

TABLE 6 Mechanical properties of the polymer networks according to polymerization method B) 25° C. 60° C. 100° C. μ_(PPDL) E σ_(b) ε_(b) E σ_(b) ε_(b) E σ_(b) ε_(b) Designation [wt %] [MPa] [MPa] [%] [MPa] [MPa] [%] [MPa] [MPa] [%] P-PPDL(4)-PCL(20, 75) 25 245 ± 5  17.2 ± 4.4  160 ± 84  3.7 ± 0.4 3.8 ± 0.6 180 ± 25  2.03 ± 0.39 1.41 ± 0.51 90 ± 20 P-PPDL(4)-PCL(20, 60) 40 270 ± 18 9.7 ± 0.7 4.3 ± 0.5 6.1 ± 0.4 1.1 ± 0.2 70 ± 12 1.54 ± 0.20 0.70 ± 0.04 60 ± 10 P-PPDL(4)-PCL(20, 50) 50 200 ± 10 12.8 ± 0.8   11 ± 1.7 10.1 ± 6.7  1.2 ± 0.3 30 ± 15 1.25 ± 0.05 0.79 ± 0.18 80 ± 14 P-PPDL(4)-PCL(20, 40) 60 289 ± 34 8.0 ± 1.0 3.3 ± 0.6 6.8 ± 2.9 1.0 ± 0.1 40 ± 39 1.58 ± 0.56 0.60 ± 0.37 45 ± 22 P-PPDL(4)-PCL(20, 25) 75 273 ± 11 11.7 ± 0.65 28 ± 11 26.0 ± 2.1  2.5 ± 2.9 30 ± 8  2.19 ± 0.17 1.06 ± 0.03 65 ± 2  P-PPDL(4)-PCL(20, 12) 88 121 ± 4  8.2 ± 0.4 60 ± 11 22.8 ± 4.8  2.7 ± 0.4 23 ± 10 3.62 ± 0.64 1.24 ± 0.68 52 ± 15 P-PPDL(4)-PCL(8, 75) 25  121 ± 4.2 8.3 ± 3.7 63 ± 11 6.69 ± 1.68 1.5 ± 0.8 48 ± 14 4.46 ± 1.12 1.43 ± 0.55 44 ± 2  P-PPDL(4)-PCL(8, 60) 40 181 ± 15 8.8 ± 1.0 25 ± 30 9.56 ± 6.23 1.3 ± 0.6 20 ± 3  2.52 ± 0.58 0.56 ± 0.50 30 ± 20 P-PPDL(4)-PCL(8, 50) 50 126 ± 30 9.9 ± 1.6 90 ± 24 11.7 ± 1.02 2.6 ± 0.4 46 ± 12 4.69 ± 0.29 1.53 ± 0.58 40 ± 13 P-PPDL(4)-PCL(8, 40) 60 241 ± 10 7.0 ± 1.4 4 ± 1 21.4 ± 4.4  1.2 ± 0.3 9 ± 4 1.89 ± 0.16 0.62 ± 0.03 42 ± 7  P-PPDL(4)-PCL(8, 25) 75 203 ± 25 9.4 ± 1.1 37 ± 38 23.9 ± 1.2  2.0 ± 0.2 18 ± 4  2.2 ± 0.3 0.45 ± 0.24 22 ± 13

Triple-Shape-Memory Properties of the Polymer Networks Experiment A

In both synthesis methods (A and B), the permanent shape (1. shape) is fixed by the cross-linking. The first programming is performed (2. shape) by bending a sample end perpendicularly at 100° C. and subsequent cooling to 60° C. The second programming (3. shape) is performed by perpendicularly bending the second sample end at 60° C. and subsequent cooling to 0° C. When immersing a test sample programmed in this way in a water bath having a temperature of 60° C., the sample side with the lower T_(switch) (2. shape) is initially recovered. This process requires that the switching temperature in the test sample is reached and lasts only for several seconds. The other sample side remains unchanged. The second sample side is also recovered to form an overall planar body (1. shape) by increasing the temperature of the water bath or by immersing the sample in a second water bath at 100° C.

Experiment B

The triple-shape-memory effect is quantitatively investigated by cyclic thermo-mechanical tensile tests, as described in Bellin et al. (see above). The shape-memory properties of the networks of PPDL(y) and PCL(x) with varying molar mass, as determined by tension-controlled, cyclic thermo-mechanical tensile tests, are listed in Table 7. The investigations show that these materials have stretch fixation and stretch return ratios of more than 90% in all cycles.

The employed polymers may be biostable or biodegradable. Multiblock copolymers which have a switching temperature in the range of the human body temperature are known for medical applications.

TABLE 7 Triple-shape-memory properties of the polymer networks according to the poly-condensation method A. R_(f) and R_(r) are averaged values from the cycles 2 to 5. The switching temperatures are averaged values from all 5 cycles. R_(f)(C→B) R_(f)(B→A) R_(r)(A→B) R_(r)(A→C) T_(sw1) T_(sw2) Designation [%] [%] [%] [%] [° C.] [° C.] T-PPDL(4)-PCL(20, 75) 74.5 ± 1.0 99.0 ± 0.1 56.2 ± 1.0 96.3 ± 7.0 66.0 ± 0.8 85.3 ± 1.1 T-PPDL(4)-PCL(20, 60) 80.1 ± 0.5 98.2 ± 0.1 81.1 ± 0.7 101.0 ± 0.5  61.0 ± 0.5 84.4 ± 0.5 T-PPDL(4)-PCL(20, 50) 72.5 ± 0.8 97.6 ± 0.2 80.5 ± 1.0 99.0 ± 1.0 61.1 ± 0.3 85.4 ± 0.3 T-PPDL(4)-PCL(20, 40) 82.1 ± 1.6 96.3 ± 0.1 85.1 ± 0.7 99.9 ± 3.2 59.2 ± 0.4 86.2 ± 0.5 T-PPDL(4)-PCL(20, 25) 91.5 ± 0.1 91.4 ± 1.0 78.8 ± 0.8 98.5 ± 2.2 62.1 ± 0.7 85.8 ± 0.5 T-PPDL(4)-PCL(8, 75) 17.6 ± 0.9 94.2 ± 1.4 88.0 ± 2.1 99.8 ± 0.6 39.9 ± 0.7 70.5 ± 0.1 T-PPDL(4)-PCL(8, 60) 64.2 ± 2.8 96.2 ± 0.3 88.2 ± 0.9 101.1 ± 1.6  48.0 ± 0.4 76.3 ± 0.4 T-PPDL(4)-PCL(8, 50) 75.2 ± 0.6 95.7 ± 0.3 84.1 ± 0.7 100.1 ± 0.5  55.4 ± 0.8 81.8 ± 0.3 T-PPDL(4)-PCL(8, 40) 86.6 ± 0.2 91.6 ± 0.2 88.3 ± 2.1 99.1 ± 3.8 56.5 ± 0.9 83.9 ± 0.4 T-PPDL(4)-PCL(8, 25) 93.8 ± 0.3 89.5 ± 0.2 80.2 ± 1.0 100.1 ± 2.6  61.1 ± 0.6 84.1 ± 0.4 T-PPDL(4)-PCL(4, 75)  2.0 ± 0.9 97.7 ± 0.1 76.5 ± 0.8 99.8 ± 0.3 36.7 ± 0.4 68.8 ± 0.3 T-PPDL(4)-PCL(4, 60) 75.5 ± 1.3 95.2 ± 0.3 81.1 ± 1.5 100.5 ± 1.2  48.5 ± 0.5 82.1 ± 1.1 T-PPDL(4)-PCL(4, 50) 84.9 ± 1.0 93.2 ± 3.7 68.1 ± 2.3 100.5 ± 0.8  48.0 ± 1.0 76.4 ± 1.0 T-PPDL(4)-PCL(4, 40) 82.0 ± 0.8 92.0 ± 0.3 75.6 ± 4.3 99.2 ± 1.0 56.3 ± 0.9 75.9 ± 0.1 T-PPDL(4)-PCL(4, 25) 93.1 ± 0.2 81.7 ± 4.1 83.8 ± 1.7 99.4 ± 2.4 59.5 ± 1.2 83.1 ± 0.4

Experiment C

For determining the one-step programming properties of the triple-shape-memory networks, the sample is stretched at the temperature T_(high) from the permanent shape C with the elongation ε_(C) into the shape ε⁰ _(A). After a waiting period of seven minutes, the sample is cooled under controlled tension with a cooling grade of 5 K·min⁻¹, whereby the sample acquires the elongation ε⁰ _(Aload). The sample is relaxed after 10 minutes, which results in the elongation ε_(A) and the shape A, respectively. The sample is subsequently recovered, as described in Bellin et al.

$\begin{matrix} {{R_{f}(N)} = \frac{{ɛ_{A}(N)} - {ɛ_{C}\left( {N - 1} \right)}}{{ɛ_{Aload}(N)} - {ɛ_{C}\left( {N - 1} \right)}}} & (1) \\ {{R_{r}(N)} = \frac{{ɛ_{A}(N)} - {ɛ_{C}(N)}}{{ɛ_{A}(N)} - {ɛ_{C}\left( {N - 1} \right)}}} & (2) \end{matrix}$

TABLE 8 Shape-memory properties of the polymer networks according to the poly-condensation method A after one-step programming. R_(f) R_(r) T_(sw1) T_(sw2) Designation [%] [%] [° C.] [° C.] T-PPDL(4)-PCL(20, 60) 97.2 ± 0.4 98.8 ± 0.8 60.6 ± 0.1 80.2 ± 0.6 T-PPDL(4)-PCL(8, 60) 98.2 ± 0.2 98.2 ± 0.9 49.8 ± 0.2 75.4 ± 0.4 T-PPDL(4)-PCL(4, 50) 95.8 ± 0.3 99.3 ± 0.2 46.5 ± 0.8 78.3 ± 0.3

Experiment D

For determining the triple-shape-memory properties with cold stretching, the sample is stretched at the temperature T_(low) from the permanent shape C with the elongation ε_(C) into the shape ε⁰ _(A), kept under tension for five minutes and then relaxed, whereby the sample acquires the elongation ε_(A) and the shape A, respectively. The recovery of the sample is then performed as described in Bellin et al. The cycle is repeated four times, the stretch fixation ratio R_(f) and the stretch recovery ratio R_(r) in the cycle N are determined in the manner described in experiment C.

TABLE 9 Shape-memory properties of the polymer networks according to the poly-condensation method A after cold stretching. R_(f) R_(r) T_(sw1) T_(sw2) Designation [%] [%] [° C.] [° C.] T-PPDL(4)-PCL(20, 75) 78.8 ± 0.2 99.8 ± 0.3 62.1 ± 0.1 83.5 ± 0.5 T-PPDL(4)-PCL(20, 50) 76.9 ± 0.3 99.9 ± 1.1 60.3 ± 0.3 75.8 ± 0.5 T-PPDL(4)-T-PCL(8, 50) 72.2 ± 0.3 99.7 ± 0.2 56.1 ± 0.6 82.6 ± 0.4 PPDL(4)-PCL(4, 50) 64.8 ± 0.3 97.7 ± 0.5 47.8 ± 0.6 81.5 ± 0.3

Experiment E

For determining the shape-memory properties, a fourfold cyclic thermo-mechanical experiment was created. The sample was hereby stretched at T_(prog) from the permanent shape C with the elongation ε_(C) into the shape ε⁰ _(A) (100% and 150%, respectively), kept under tension for five minutes and subsequently cooled under controlled tension with a cooling grade of 5 K·min⁻¹, whereby the sample attains the elongation ε⁰ _(Aload). After 10 minutes, the sample is relaxed, resulting in the elongation ε_(A) and the shape A, respectively. Recovery is performed by heating to T_(high)=115° C. at a heating rate of 1 K·min⁻¹. To eliminate the previous thermal history of the sample, T_(prog)=90° C. was selected in the first cycle. In the subsequent three cycles, 30, 60 and 90° C. were selected for T_(prog). The switching temperatures were determined in the same manner as described in experiment B.

TABLE 10 Temperature memory properties of the polymer network according to the poly-condensation method A. T_(prog) = 30° C. T_(prog) = 60° C. T_(prog) = 90° C. R_(f) R_(r) T_(sw) R_(f) R_(r) T_(sw) R_(f) R_(r) T_(sw) Designation [%] [%] [° C.] [%] [%] [° C.] [%] [%] [° C.] T-PPDL(4)-PCL(8, 25) 81.9 98.1 29.2 93.4 96.9 59.0 98.6 99.6 78.4 T-PPDL(4)-PCL(4, 40) 81.6 100.2 28.6 91.4 97.3 59.3 97.4 99.9 75.0 T-PPDL(4)-PCL(4, 25) 81.1 97.6 29.1 92.0 101.8 59.0 98.4 101.0 81.1

Experiment F

For determining the reversible triple-shape-memory properties under constant tension, the sample is stretched at T_(high) from the permanent shape C with the tension σ_(C) into the shape ε⁰ _(C). After waiting for 10 minutes, the sample is cooled under constant tension σ_(C) to T_(low) with a cooling grade between 0.1 and 2 K/min, resulting in a two-stage elongation of the sample to the shapes B and A with the elongations ε_(B) and ε_(A). After 10 minutes at T_(low), the sample is heated to T_(high) with a heating rate of 1 K/min, whereby the shapes B and C are stepwise recovered.

TABLE 11 Reversible triple-shape-memory properties of the polymer networks according to the poly-condensation method A under constant tension. σ_(c) T_(sw)(C→B) T_(sw)(B→A) T_(sw)(A→B) T_(sw)(B→C) Δε_(rel)(A→B) Δε_(rel)(B→C) Network-ID [MPa] [° C.] [° C.] [° C.] [° C.] [%] [%] T-PPDL(4)- 0.6 69.4 37.3 45.3 78.5 9 91 PCL(8, 50) T-PPDL(3)- 1.0 60.5 32.6 43.2 75.7 22 78 PCL(8, 50)

Preparation of Multilayer Materials

The polymer networks prepared with the polymerization method B were synthesized in layers having a thickness of 0.5 mm. The individual polymer layers are programmed according to the Experiment B. The degree of this mono-directional stretching can be selected over a wide range. In a demonstration experiment, two layers were glued together, wherein one layer was pre-stretched by 20%. However, the programming direction of the layers may also deviate from one another after gluing. Cyanacrylate chemistry was used for gluing to attain a solid and permanent bond between the two layers.

The expected mechanical properties of the composite materials can be calculated with the help of computer modeling studies. These modeling studies provide details for programming and stacking the layers for attaining particular shape changes of the material.

FIG. 3 shows layer systems made of triple-shape-memory polymers. FIG. 4 shows individual layers with a 3-D profile, which can be programmed in a planar structure and form a layer system in conjunction with other planar or planar-programmed layers. FIG. 5 shows a layer system of layers stacked above one another on a surface X; the stacked layers are cut at arbitrary angles into layers and can then be stacked to form new layer systems. FIG. 6 shows reversible triple-shape-memory properties of the network a: T-PPDL(4)-PCL(8,50) at a tension of 0.6 MPa; b: T-PPDL(3)-PCL(8,50) at a tension of 1 MPa. 

We claim:
 1. A method for producing layer systems from polymer shape-memory materials, comprising the steps of: a) providing at least two layers of polymer shape-memory materials; and b) producing a layer system of the at least two layers by reactive gluing, wherein the two layers are differentiated from each other in their programming, shape and composition.
 2. The method according to claim 1, wherein the layers are planar or are provided with a three-dimensional profile.
 3. The method according to claim 1, wherein the layers have a different layer thickness.
 4. The method according to claim 1, wherein the layers are made of a polymer matrix with integrated shape-memory polymer fibers.
 5. The method according to claim 1, wherein the layers have different degrees of programming, in particular degrees of stretching, and/or a different programming orientation.
 6. The method according to claim 1, wherein the layers are programmed mono-directionally or multi-directionally. 